WO2023138595A1 - Pipeline à haute résistance résistant à la corrosion à l'hydroxyde de sodium et son procédé de fabrication - Google Patents

Pipeline à haute résistance résistant à la corrosion à l'hydroxyde de sodium et son procédé de fabrication Download PDF

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Publication number
WO2023138595A1
WO2023138595A1 PCT/CN2023/072769 CN2023072769W WO2023138595A1 WO 2023138595 A1 WO2023138595 A1 WO 2023138595A1 CN 2023072769 W CN2023072769 W CN 2023072769W WO 2023138595 A1 WO2023138595 A1 WO 2023138595A1
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corrosion
pipeline
resistant layer
present
layer
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PCT/CN2023/072769
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English (en)
Chinese (zh)
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闫博
焦四海
王治宇
李占杰
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宝山钢铁股份有限公司
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Publication of WO2023138595A1 publication Critical patent/WO2023138595A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B21B1/28—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by cold-rolling, e.g. Steckel cold mill
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/30—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process
    • B21B1/32—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process in reversing single stand mills, e.g. with intermediate storage reels for accumulating work
    • B21B1/34—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process in reversing single stand mills, e.g. with intermediate storage reels for accumulating work by hot-rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/30—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process
    • B21B1/32—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process in reversing single stand mills, e.g. with intermediate storage reels for accumulating work
    • B21B1/36—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process in reversing single stand mills, e.g. with intermediate storage reels for accumulating work by cold-rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/30—Stress-relieving
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
    • F16L58/00—Protection of pipes or pipe fittings against corrosion or incrustation
    • F16L58/02—Protection of pipes or pipe fittings against corrosion or incrustation by means of internal or external coatings
    • F16L58/04—Coatings characterised by the materials used
    • F16L58/08—Coatings characterised by the materials used by metal
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
    • B21B2001/386—Plates
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
    • B21C37/08—Making tubes with welded or soldered seams
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E30/00—Energy generation of nuclear origin
    • Y02E30/30—Nuclear fission reactors

Definitions

  • the invention relates to a pipeline and a manufacturing method thereof, in particular to a sodium hydroxide corrosion-resistant high-strength pipeline and a manufacturing method thereof.
  • the alkaline cleaning process of the membrane pool is usually used for treatment.
  • the dosing pipes, flushing pipes, and pipes from the membrane pool to the neutralization pool used in the alkali cleaning process of the membrane pool are easily corroded by sodium hydroxide. Therefore, in order to prevent these pipes from being corroded by sodium hydroxide as far as possible, 304 and 316L stainless steel materials are usually used to manufacture such pipes.
  • 304 and 316L stainless steel Compared with carbon steel, the structural strength of 304 and 316L stainless steel is lower. Under the same working conditions, the required thickness is larger, which will lead to an increase in the amount of materials used; at the same time, the welding and machining of 304 and 316L stainless steel are more difficult; moreover, 304 and 316L stainless steel itself contains more precious metal elements such as Cr, Ni, Mo, etc., resulting in a relatively high cost of pure stainless steel in the process of production, production, and installation.
  • the present invention expects to obtain a new pipeline.
  • the pipeline adopts a reasonable design, which can form a corrosion resistant layer resistant to sodium hydroxide corrosion on the surface of the carbon steel base layer, and finally form a pipeline with both sodium hydroxide corrosion resistance, good mechanical properties and high economy, which has great economic and social benefits.
  • One of the purposes of the present invention is to provide a new pipeline.
  • the pipeline adopts a reasonable design, which can form a corrosion-resistant layer resistant to sodium hydroxide corrosion on the surface of the carbon steel base, and finally form a pipeline with corrosion resistance to sodium hydroxide, good mechanical properties and high economy.
  • the pipeline described in the present invention can solve the essential pain points of 304, 316L stainless steel or carbon steel used in the sodium hydroxide corrosive medium environment of the current water supply plant station, meet the pipeline equipment used in the sodium hydroxide medium environment by the water supply plant station, and continuously improve the corrosion resistance and mechanical properties of the pipeline, and greatly improve the applicability, safety, and durability of these pipeline equipment. At the same time, it avoids secondary pollution to water quality, which has great economic and social benefits.
  • the present invention provides a pipeline, the pipeline has a corrosion-resistant layer and a base layer in the thickness direction, the corrosion-resistant layer is at least located on the inner wall of the pipeline, and the corrosion-resistant layer also contains the following chemical elements in wt% in addition to Fe and unavoidable impurities:
  • the corrosion-resistant layer contains the following chemical elements in wt %:
  • the balance is Fe and unavoidable impurities
  • the sodium hydroxide corrosion resistance of the corrosion-resistant layer In the pipeline of the present invention, in order to ensure the sodium hydroxide corrosion resistance of the pipeline, the sodium hydroxide corrosion resistance of the corrosion-resistant layer must first be ensured.
  • the working condition of the sodium hydroxide corrosive medium in the existing water supply station is: there is sodium hydroxide with a mass concentration of 0-30% in the transport medium, and its temperature is between 0-40°C.
  • the inventor optimized the chemical element composition of the pipeline corrosion-resistant layer, in which a certain amount of Ti element was added, and a special corrosion-resistant equivalent formula and requirements were designed to control Cr, Mo, N and Ti satisfies Cr+2.8 ⁇ Mo+16 ⁇ N+2 ⁇ Ti ⁇ 22.0%, in order to further reduce the susceptibility to intergranular corrosion, prevent stress corrosion of pipeline equipment in alkali cleaning process, and avoid corrosion of weld seam by sodium hydroxide solution when the temperature continues to be higher.
  • the design principle of the chemical elements of the corrosion-resistant layer is as follows:
  • C is a strong austenite-forming element, which can replace nickel to a certain extent, promote the formation of austenite, stabilize the austenite structure, and increase the strength of stainless steel.
  • the content of C element should not be too high.
  • the carbon content is too high, the combination of carbon and chromium will form chromium-rich carbides at the grain boundaries, resulting in intergranular corrosion. Therefore, in order to exert the beneficial effects of the C element, in the corrosion-resistant layer of the present invention, the mass percentage of the C element is controlled to satisfy 0 ⁇ C ⁇ 0.05%.
  • Si element is mainly used for deoxidation during the smelting process, so generally a certain amount of silicon needs to be added. However, it should be noted that the Si element content should not be too high. When the Si content is too high, the solubility of nitrogen will be reduced. Therefore, in the corrosion-resistant layer of the present invention, the mass percentage of Si element is controlled between 0.3-0.6%.
  • the Mn element is a strong austenite stabilizing element, and can increase the solubility of nitrogen in steel.
  • manganese has a negative impact on the corrosion resistance of austenitic stainless steel at the same time. Therefore, considering the beneficial effects and adverse effects of the Mn element, in the corrosion-resistant layer of the present invention, the mass percentage of the Mn element is controlled between 0.5-2.0%, preferably 1.0-2.0%, more preferably 1.0-1.36%.
  • Ni is the most important element for forming and stabilizing the austenite phase. Adding an appropriate amount of Ni element can ensure the formation of austenite structure of the steel at room temperature. However, the price of nickel is expensive, in order to ensure a relatively low cost, it is not appropriate to add excessive nickel to the steel. Therefore, in the corrosion-resistant layer of the present invention, the mass percentage of Ni element is controlled between 8.00-14.00%, preferably 8.00-10.00%.
  • Cr In the corrosion-resistant layer of the present invention, Cr is the guarantee to obtain stainless steel's rust resistance and corrosion resistance. Generally, the minimum chromium content to obtain corrosion resistance is 10.5%. Since chromium is an element that significantly enhances corrosion resistance, in order to ensure good corrosion resistance, the content of chromium in the steel of the present invention is controlled above 16.0%. However, it should be noted that chromium is also the main ferrite-forming element, and too high a content of chromium will make it difficult to ensure that the corrosion-resistant layer obtains austenite structure at room temperature. Therefore, in the corrosion-resistant layer of the present invention, the mass percentage of Cr element is controlled between 16.00-19.00%.
  • Mo in the corrosion-resistant layer of the present invention, Mo is an important element to improve corrosion resistance, and its mechanism is to stabilize the passivation film and promote the enrichment of chromium in the passivation film; in addition, molybdenum can also cooperate with nitrogen to further improve pitting resistance, so the main effect of adding molybdenum is to improve corrosion resistance.
  • the Mo element content should not be too high, too high molybdenum content will increase the cost of the alloy, in order to ensure a relatively low cost, in the corrosion-resistant layer of the present invention, the mass percentage of Mo element is controlled between 2.00-3.50%, preferably 2.00-3.00%.
  • N is a very strong element that forms, stabilizes and expands the austenite zone. Adding an appropriate amount of N element can effectively improve the pitting corrosion resistance of stainless steel. However, when the nitrogen content in the steel is too high, it will increase the risk of nitrogen-containing intermetallic phase formation, and at the same time increase the difficulty of smelting and hot processing, making it difficult to produce. Therefore, in the corrosion-resistant layer of the present invention, the mass percentage of N element is controlled between 0.02-0.20%, preferably 0.02-0.10%.
  • Ti is a stabilizing element of titanium and nitrogen compounds. Adding an appropriate amount of Ti element in the steel can effectively prevent the decrease in corrosion resistance caused by the reduction of chromium concentration caused by the formation of compounds between chromium and carbon; in addition, adding an appropriate amount of Ti element can also prevent pitting corrosion caused by MnS.
  • the Ti element content in the steel should not be too high. When the Ti element content in the steel is too high, it will not only increase the risk of forming intermetallic phases containing titanium and nitrogen, but also reduce the thermoplasticity of the steel, increase the difficulty of smelting and hot processing, and make it difficult to produce. Therefore, in the corrosion-resistant layer of the present invention, the mass percentage of Ti element is controlled between 0.01-0.2%, preferably 0.1-0.2%.
  • the corrosion-resistant layer of the pipeline while controlling the mass percentage of a single chemical element, the elements Cr, Mo, N and Ti are further controlled to satisfy: Cr+2.8 ⁇ Mo+16 ⁇ N+2 ⁇ Ti ⁇ 22.0%. Each element in the formula is substituted into the mass percentage of the corresponding element. Through such control, it can be further ensured that the corrosion-resistant layer has quite excellent corrosion resistance in a sodium hydroxide environment.
  • unavoidable impurities include: S ⁇ 0.030%; P ⁇ 0.045%.
  • both P and S are unavoidable impurity elements.
  • the lower the content of the impurity elements in the steel the better, if conditions permit.
  • the base layer contains the following chemical elements in wt %:
  • the balance is Fe and unavoidable impurities.
  • the base layer also contains at least one of the following chemical elements:
  • the chemical element composition of the base carbon steel needs to ensure both higher strength and better machinability.
  • C is an austenite stabilizing element, which can play a role of solid solution strengthening in steel, and can obviously improve the strength of steel.
  • the content of C element in the steel should not be too high.
  • the mass percentage of the C element is controlled between 0.01-0.20%, preferably 0.10-0.20%.
  • Si In the base layer of the present invention, adding Si element to the steel can effectively improve the purity and deoxidation of the steel.
  • Si element can play a solid solution strengthening effect in steel, but Si element is not conducive to the welding performance of the material; in the present invention, the silicon content of the base carbon steel is controlled to be less than or equal to 0.3%, which will not have any impact on the corrosion resistance of the corrosion resistance layer, and the base carbon steel has good welding performance. Therefore, in the base layer of the present invention, the mass percentage of Si element is controlled between 0.10-0.30%.
  • Mn In the base layer of the present invention, adding an appropriate amount of Mn element to the steel can delay the pearlite transformation, reduce the critical cooling rate, and improve the hardenability of the steel; at the same time, the Mn element also has the effect of solid solution strengthening, which is the main solid solution strengthening element in the steel.
  • the Mn element should not be added too much. When the Mn element content in the steel is too high, segregation bands and martensitic structures are prone to appear, which have an adverse effect on the toughness of the steel, and the appearance of the segregation band will also reduce the corrosion resistance of the steel.
  • the amount of Mn added mainly depends on the strength level of the steel.
  • the manganese content in low-carbon micro-alloyed steel does not exceed 1.50%.
  • the Mn element contained in the base carbon steel will not have adverse effects on the corrosion-resistant layer.
  • the mass percentage of Mn element is controlled between 0.50-1.50%, preferably 1.00-1.50%.
  • Al is a strong deoxidizing element. Al is added to ensure that the oxygen content in the steel is as low as possible. After deoxidation, the excess Al and N elements in the steel can combine to form AlN precipitates, thereby improving the strength of the steel and refining the austenite grain size of the steel during heat treatment. However, it should be noted that if the Al content is too high, it is easy to generate Al oxide inclusion defects. Based on this, in the base layer of the present invention, the mass percentage of Al element is controlled between 0.02-0.03%.
  • Ti is a strong carbide-forming element. Adding a small amount of Ti in the steel is beneficial to fixing N in the steel.
  • the TiN formed by the combination of Ti and N can prevent the austenite grain from growing too much when the base material is heated, and refine the raw material. Austenite grain size.
  • Ti can also be combined with carbon and sulfur in steel to form TiC, TiS, Ti 4 C 2 S 2 , etc., which can exist in the form of inclusions and second phase particles.
  • these carbonitride precipitates of Ti can also prevent grain growth in the heat-affected zone during welding and improve welding performance.
  • the mass percentage of Ti element is controlled between 0.005-0.018%.
  • Nb is a strong carbide-forming element.
  • a small amount of niobium is added to the steel mainly to increase the recrystallization temperature to match the higher final rolling temperature of the composite plate formed by the base layer slab and the corrosion-resistant layer slab assembly during the subsequent rolling process, so that the grains of the base layer are refined after rolling in the recrystallization and non-recrystallization areas, so as to improve the low temperature impact toughness of the base layer.
  • the mass percentage of Nb element is controlled between 0.005-0.020%.
  • element N In the base layer of the present invention, element N can form second-phase particles with titanium and aluminum to refine grains and improve strength. However, when the mass percentage of N element is too high, the amount of TiN generated will be too large and the particles will be too coarse, which will affect the plasticity of the base carbon plate of the composite material of the present invention. Based on this, in the base layer of the present invention, the mass percentage of N element is controlled to be N ⁇ 0.006%.
  • B can greatly improve the hardenability of steel.
  • the high corrosion-resistant composite plate corrosion-resistant layer slab + base slab
  • the addition amount of element B is set to 0 ⁇ B ⁇ 0.0003%.
  • Ni is an element that stabilizes austenite, and it has a certain effect on improving the strength of steel.
  • adding an appropriate amount of Ni to steel, especially adding an appropriate amount of Ni to quenched and tempered steel can greatly improve the low temperature impact toughness of steel.
  • an excessively high Ni content will increase the carbon equivalent and affect the welding performance; at the same time, Ni is a rare metal, resulting in waste of resources and increase in cost.
  • the addition amount of Ni element is controlled to satisfy 0 ⁇ Ni ⁇ 0.20%.
  • the segregation tendency of the Cr element is smaller than that of Mn.
  • Mn content of the base carbon steel is high, and when there are obvious segregation bands and banded structures in the steel, the Mn content can be appropriately reduced, and the insufficient part can be replaced by Cr.
  • adding an appropriate amount of Cr element to the base carbon steel is also beneficial to inhibit the diffusion of Cr in the corrosion-resistant layer to the base.
  • too high Cr content will affect the phase transition temperature of the substrate and affect the mechanical properties of the substrate. Based on this, in the base layer of the present invention, the Cr element of 0 ⁇ Cr ⁇ 0.20% can be added.
  • Mo element can significantly refine grains and improve the strength and toughness of steel.
  • Mo can also reduce the temper brittleness of steel, and at the same time, very fine carbides can be precipitated during tempering, which can significantly strengthen the steel matrix.
  • the addition of Mo element is also beneficial to suppress the self-temper brittleness of the steel plate that is easy to occur during the air cooling process.
  • an excessively high Mo content will increase the carbon equivalent, affect welding performance, and lead to resource waste and cost increase. Based on this, in the base layer of the present invention, the addition amount of Mo element is controlled to satisfy 0 ⁇ Mo ⁇ 0.10%.
  • unavoidable impurities include: S ⁇ 0.010%; P ⁇ 0.015%.
  • P and S are unavoidable impurity elements in the base layer.
  • S will combine with Mn in the steel to form plastic inclusion manganese sulfide, which is especially unfavorable to the transverse plasticity and toughness of the steel. Therefore, the content of S element in the base layer should be as low as possible.
  • P is also a harmful element in steel, which will seriously damage the plasticity and toughness of the steel plate.
  • both S and P are unavoidable impurity elements, and the lower the better, considering the actual steelmaking level of the steel plant, in the base layer of the present invention, the S and P elements are controlled to satisfy: S ⁇ 0.010%; P ⁇ 0.015%.
  • the thickness of the single-layer corrosion-resistant layer accounts for 0.5-20% of the total thickness of the pipeline, more preferably the thickness of the single-layer corrosion-resistant layer accounts for 1.2%-16.7% of the total thickness of the pipeline. That is to say, if both the inner surface and the outer surface of the pipeline have corrosion-resistant layers, the thickness of each corrosion-resistant layer accounts for 0.5-20% of the total thickness of the pipeline. If only the inner surface of the pipeline has a corrosion-resistant layer, the thickness of the corrosion-resistant layer accounts for 0.5-20% of the total thickness of the pipeline.
  • the selection of the thickness of the corrosion-resistant layer plays a crucial role in obtaining good corrosion resistance, mechanical properties and formability of the pipeline described in the present invention.
  • the thickness of the single-layer corrosion-resistant layer is preferably controlled to account for 0.5-20% of the total thickness of the pipeline, and more preferably the thickness of the single-layer corrosion-resistant layer accounts for 1.2-16.7% of the total thickness of the pipeline.
  • the microstructure of the base layer is ferrite+pearlite, or ferrite+pearlite+bainite; the microstructure of the corrosion-resistant layer is austenite.
  • the yield strength of the pipeline is ⁇ 426MPa
  • the tensile strength is ⁇ 585MPa
  • the elongation is ⁇ 35%
  • the uniform corrosion rate (ie average corrosion rate) of the corrosion-resistant layer is ⁇ 0.05mm/year in an environment with a temperature ⁇ 40°C and a sodium hydroxide concentration ⁇ 30wt%.
  • another object of the present invention is to provide a method for manufacturing the above-mentioned pipeline, which is simple and feasible, and can effectively prepare the above-mentioned pipeline.
  • the present invention proposes the method for manufacturing above-mentioned pipeline, and this method comprises the steps:
  • the corrosion-resistant layer slab and the base slab are assembled to obtain a composite slab; wherein, the preferred single-layer corrosion-resistant layer thickness accounts for 0.5-20% of the composite slab's total thickness, and more preferably the single-layer corrosion-resistant layer thickness accounts for 1.2-16.7% of the total pipeline thickness (the single-layer corrosion-resistant layer/pipeline total thickness ratio in the finished pipeline is basically the same as the thickness ratio in this step);
  • Heating and rolling the heating temperature is 1150-1230°C, and then multi-pass rolling is carried out, the total reduction rate is not lower than 90%, and the final rolling temperature is not lower than 900°C;
  • smelting and casting can be designed according to the chemical composition to prepare the corrosion-resistant layer slab and the base layer slab, and then the two can be assembled to obtain a high-corrosion-resistant composite plate (corrosion-resistant layer plate + base layer plate).
  • the obtained high-corrosion-resistant composite plate is further heated, rolled, and coiled to obtain a hot-rolled coil with a composite interlayer structure. After the surface treatment of the hot-rolled coil, the pipe of the present invention can be obtained.
  • the inventors optimized the heating and rolling process in step (3) to ensure that a transition layer structure of a certain thickness can be formed between the corrosion-resistant layer and the base layer through heating, rolling, etc., so as to realize the complete metallurgical combination of the corrosion-resistant layer and the base layer, thereby improving the applicability and economy of the material while ensuring the corrosion resistance and mechanical properties of sodium hydroxide.
  • the prepared corrosion-resistant layer slab and the base slab can be pretreated, and the bonding surface of the slab is welded and sealed around, and the joint surface after welding and sealing is vacuumized to complete the slab assembly.
  • step (5) surface treatment is carried out on the hot-rolled coil, and pickling or mechanical descaling can be used.
  • step (6) conventional spiral welded pipe or straight seam welded pipe can be used for forming and welding, and the welding method can be submerged arc welding, gas metal arc welding pipe, tungsten inert gas shielded welding, plasma arc welding, electrode arc welding, high frequency welding or laser welding.
  • step (3) the finishing rolling temperature is controlled to be 920-1050°C.
  • a preheating step is further included between step (2) and step (3), wherein the preheating temperature is 1150-1230°C.
  • the composite slab obtained by forming the billet can be heated at a temperature of 1150-1230°C, so that the corrosion-resistant layer on the surface of the composite slab can obtain a uniform austenitized structure, try to completely dissolve the carbides that may exist originally, and at the same time completely or partially dissolve the compounds of alloying elements such as niobium and titanium in carbon steel; The elements of the corrosion layer and the carbon steel base layer diffuse at the interface to form a stable transition layer, and then slowly cool to room temperature.
  • cold rolling and annealing are also included between step (5) and step (6); preferably, the annealing temperature is 900-1000°C.
  • step (5) a step of cold rolling and annealing can be added between step (5) and step (6), which can be cold-rolled to the target thickness and then annealed.
  • the inventor designs the composition of the corrosion-resistant layer and the base layer, and the ratio design of the two, and uses a rolling process to form a corrosion-resistant layer resistant to sodium hydroxide on the surface of the carbon steel plate of the base layer, and finally obtain a strip with corrosion resistance to sodium hydroxide, good mechanical properties and high economic efficiency, and then process it into a pipeline, which is used for pipeline equipment used in the environment of sodium hydroxide corrosive medium in water supply stations.
  • composition design of the corrosion-resistant layer and the base layer needs to meet the comprehensive performance of the material.
  • the composition of the corrosion-resistant layer needs to be designed according to the characteristics of sodium hydroxide corrosion to meet the requirements of corrosion resistance under service conditions.
  • carbon steel composition of the base layer in addition to meeting the requirements of mechanical properties, it is also necessary to consider that when the carbon content of the transition layer obtained by combining the base layer and the corrosion-resistant layer is high, there will be a lack of stabilizing elements, and there will be an obvious decarburization layer on the carbon steel side at the interface junction.
  • the ratio of the corrosion-resistant layer to the base metal and the difference in material properties will make it difficult to control the heating process, rolling process, and heat treatment process.
  • the temperature is not uniform during the heating process, which causes deformation and swelling, which makes it impossible to combine with the base layer.
  • the inventor considers the working conditions of the current pipeline equipment in the water supply plant station under the environment of sodium hydroxide corrosive medium, through designing the components of the corrosion-resistant layer and the base layer, and designing the ratio of the two, combining the corrosion-resistant layer and the base layer into a billet, and applying suitable heating, rolling, and coiling processes, and cooperating with the pipe-making process, a pipeline with both sodium hydroxide corrosion resistance, good mechanical properties and high economy can be obtained.
  • the yield strength is ⁇ 426 MPa
  • the tensile strength is ⁇ 585 MPa
  • the average corrosion rate of the corrosion-resistant layer ⁇ 0.05mm/year in an environment with a temperature ⁇ 40°C and a sodium hydroxide concentration ⁇ 30wt%.
  • a transitional layer structure of a certain thickness is formed between the corrosion-resistant layer and the base layer through processes such as heating and rolling, which realizes the complete metallurgical combination of the corrosion-resistant layer and the base layer, so as to improve the applicability and economy of the material while ensuring the corrosion resistance and mechanical properties of sodium hydroxide.
  • the pipeline manufactured by the above-mentioned composition design and process control method can solve the essential pain point of 304, 316L stainless steel or carbon steel used in the sodium hydroxide corrosive medium environment of the water supply plant station; the pipeline can be effectively applied to the pipeline equipment used in the sodium hydroxide medium environment of the water supply plant station, such as: dosing pipelines, flushing pipelines, and membrane tank to neutralization tank pipelines in the alkaline cleaning process of membrane pools. Sex, while avoiding secondary pollution to water quality, has great economic and social benefits.
  • the pipelines of the present invention Compared with the current 304 and 316L stainless steel pipes used in the alkaline cleaning process of the membrane pool in the water supply station, the pipelines of the present invention have higher strength, simpler welding and mechanical processing, and higher economical efficiency. Compared with carbon steel pipes, the plate and strip steel pipes of the present invention can avoid the pipeline corrosion-resistant coating process, and at the same time have the corrosion resistance and durability that carbon steel pipes cannot match, and are more energy-saving, environmentally friendly and maintenance-free.
  • Fig. 1 is a schematic diagram of the interlayer structure of the pipeline according to the present invention in an embodiment.
  • Fig. 2 is a schematic diagram of the interlayer structure of the pipeline according to the present invention in another embodiment.
  • Fig. 3 and Fig. 4 are microstructure photographs of the bonding interface between the base layer and the corrosion-resistant layer of the pipeline in Example 3.
  • Table 1 lists the mass percentages of the chemical elements in the corrosion-resistant layers in the pipelines of Examples 1-7.
  • Table 2 lists the mass percentages of each chemical element in the base layer of the pipelines of Examples 1-7.
  • pipelines of Examples 1-7 of the present invention are all prepared by the following steps:
  • the composite slab is heated at a temperature of 1150-1230°C, and then multi-pass rolling is carried out within the austenite recrystallization and non-recrystallization temperature range of the base slab and the corrosion-resistant layer slab, the total reduction rate is controlled not less than 90%, the final rolling temperature is not lower than 900°C, and the final rolling temperature is between 920-1050°C.
  • Coiling after water cooling, coiling is performed at a temperature of 650-700° C. to obtain hot-rolled coils.
  • Pipe making Spiral welded pipe or straight seam welded pipe is used for forming and welding; welding methods can be selected from submerged arc welding, gas metal arc welding pipe, tungsten inert gas shielded welding, plasma arc welding, electrode arc welding, high frequency welding or laser welding.
  • the pipelines of Examples 1-7 of the present invention are all produced by the process of the above step (1)-step (6), and their chemical composition and related process parameters all meet the control requirements of the design specification of the present invention.
  • Table 3 lists the specific process parameters of the pipelines of Examples 1-7 in the steps of the above-mentioned manufacturing method.
  • the plates prepared according to the various embodiments can further prepare corresponding pipes in the pipe making process in step (6).
  • Sodium hydroxide corrosion resistance test Each embodiment 1-7 coupon is placed in the pipeline of the membrane pool alkali cleaning process of the water supply plant (temperature ⁇ 40 °C and the environment of sodium hydroxide concentration ⁇ 30wt%), take it out after 3 months and observe the surface condition of the corrosion resistance layer, measure whether there is corrosion phenomenon in the weight loss at the beginning of corrosion, calculate the annual corrosion rate of each embodiment, thus the sodium hydroxide corrosion resistance of the sample pipeline of embodiment 1-7 can be obtained.
  • Table 4 lists the test results of the microstructure, mechanical properties and sodium hydroxide corrosion resistance of the pipelines of Examples 1-7.
  • the yield strength of the pipelines of Examples 1-7 is between 426-507MPa
  • the tensile strength is between 585-650MPa
  • the elongation is between 35.8-40.0%
  • the annual corrosion rate of sodium hydroxide in the test environment is ⁇ 0.04mm/year.
  • the present invention can obtain pipes with good corrosion resistance and mechanical properties through appropriate material selection, composition design, rolling and heat treatment processes and pipe making, which can solve the essential pain points of 316 stainless steel or carbon steel used in the sodium hydroxide corrosive medium environment at present, meet the continuous improvement of pipeline equipment used in the sodium hydroxide corrosive medium environment in terms of pipeline corrosion resistance and mechanical properties, and have great economic and social benefits.
  • Fig. 1 is a schematic diagram of the interlayer structure of the pipeline according to the present invention in an embodiment.
  • the pipeline of the present invention may include: two corrosion-resistant layers on the inner surface and the outer surface of the pipeline and a carbon steel base layer in the middle.
  • Fig. 2 is a schematic diagram of the interlayer structure of the pipeline according to the present invention in another embodiment.
  • the pipeline of the present invention may include: a corrosion-resistant layer on the inner surface of the pipeline and a carbon steel base layer on the outer surface of the pipeline.
  • Fig. 3 and Fig. 4 are microstructure photographs of the bonding interface between the base layer and the corrosion-resistant layer of the pipeline in Example 3.
  • the total thickness of the pipeline is 4mm, and the thickness of its single-layer corrosion-resistant layer is 50 ⁇ m.
  • the microstructure of the base layer of the pipeline is ferrite+pearlite+bainite; the corrosion-resistant layer The microstructure is austenite; correspondingly, in the present invention, the elements of the corrosion-resistant layer and the base layer diffuse at the bonding interface to form a stable transition layer, and the diffusion distance is about 50 ⁇ m.

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Abstract

La présente invention divulgue un pipeline, qui a une couche résistante à la corrosion et une couche de base dans le sens de l'épaisseur, la couche résistante à la corrosion étant au moins située sur la paroi interne du pipeline ; et la couche résistante à la corrosion comprenant en outre, en plus du Fe et des impuretés inévitables, les éléments chimiques suivants en pourcentages en poids : 0 < C ≤ 0,05 % ; Si : 0,3-0,6 % ; Mn : 0,5-2,0 % ; Ni : 8,00-14,00 % ; Cr : 16,00-19,00 % ; Mo : 2,00-3,50 % ; N : 0,02-0,20 % ; et Ti : 0,01-0,2 %, Cr, Mo, N et Ti satisfaisant l'inéquation suivante : Cr + 2,8 × Mo + 16 × N + 2 × Ti ≥ 22,0 %. De manière correspondante, la présente invention divulgue en outre un procédé de fabrication du pipeline, lequel procédé comprend les étapes consistant à : (1) préparer une ébauche de plaque de couche résistante à la corrosion et une ébauche de plaque de couche de base ; (2) assembler l'ébauche de plaque de couche résistante à la corrosion et l'ébauche de plaque de couche de base pour obtenir une ébauche de plaque composite ; (3) chauffer et laminer, ce qui implique de chauffer l'ébauche de plaque composite à une température de 1 150-1 230 °C, le taux de réduction total n'étant pas inférieur à 90 %, et la température de laminage final n'étant pas inférieure à 900 °C ; (4) bobiner, ce qui implique après refroidissement à l'eau de bobiner celle-ci à une température de 650 à 700 °C pour obtenir une bobine laminée à chaud ; (5) soumettre la bobine laminée à chaud à un traitement de surface ; et (6) préparer un pipeline.
PCT/CN2023/072769 2022-01-21 2023-01-18 Pipeline à haute résistance résistant à la corrosion à l'hydroxyde de sodium et son procédé de fabrication WO2023138595A1 (fr)

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06235050A (ja) * 1993-02-10 1994-08-23 Nippon Steel Corp 接合強度の高いステンレスクラッド鋼材
WO2014148540A1 (fr) * 2013-03-19 2014-09-25 新日鐵住金ステンレス株式会社 Tôle d'acier plaqué comportant, comme matériau d'appariement, de l'acier inoxydable duplex qui présente une bonne performance de chauffage linéaire, et procédé permettant de fabriquer cette dernière
CN110462087A (zh) * 2017-03-29 2019-11-15 杰富意钢铁株式会社 复合钢板及其制造方法
CN113106327A (zh) * 2020-01-13 2021-07-13 宝山钢铁股份有限公司 一种高耐蚀带钢及其制造方法
US20230001504A1 (en) * 2019-11-29 2023-01-05 Baoshan Iron & Steel Co., Ltd. Carbon steel and austenitic stainless steel rolling clad plate manufacturing method therefor

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06235050A (ja) * 1993-02-10 1994-08-23 Nippon Steel Corp 接合強度の高いステンレスクラッド鋼材
WO2014148540A1 (fr) * 2013-03-19 2014-09-25 新日鐵住金ステンレス株式会社 Tôle d'acier plaqué comportant, comme matériau d'appariement, de l'acier inoxydable duplex qui présente une bonne performance de chauffage linéaire, et procédé permettant de fabriquer cette dernière
CN110462087A (zh) * 2017-03-29 2019-11-15 杰富意钢铁株式会社 复合钢板及其制造方法
US20230001504A1 (en) * 2019-11-29 2023-01-05 Baoshan Iron & Steel Co., Ltd. Carbon steel and austenitic stainless steel rolling clad plate manufacturing method therefor
CN113106327A (zh) * 2020-01-13 2021-07-13 宝山钢铁股份有限公司 一种高耐蚀带钢及其制造方法

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